CN1046565A - The thin preparation method who waits axle microstructure titanium and titanium alloy material - Google Patents
The thin preparation method who waits axle microstructure titanium and titanium alloy material Download PDFInfo
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- CN1046565A CN1046565A CN90102119A CN90102119A CN1046565A CN 1046565 A CN1046565 A CN 1046565A CN 90102119 A CN90102119 A CN 90102119A CN 90102119 A CN90102119 A CN 90102119A CN 1046565 A CN1046565 A CN 1046565A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C14/00—Alloys based on titanium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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Abstract
In the preparation of titanium and (alpha+beta) Type Titanium Alloy material, will with the hydrogen amount be the material of 0.02-2% (weight) hydrogenation under 450-900 ℃ of temperature, with greater than 60% draught processing, with this material in its aerial dehydrogenation and annealing.Under 450-800 ℃, carry out the processing of titanium material, under 550-900 ℃, carry out the processing of (alpha+beta) Type Titanium Alloy material.In the preparation of titanium, (alpha+beta) Type Titanium Alloy material and (alpha+beta) Type Titanium Alloy material, to be that the material of 0.02-2% (weight) hydrogenation is heat-treated with the hydrogen amount, wherein this material is heated being not less than under the temperature of beta transus temperature, cooling then, under 450-950 ℃ of temperature, to be not less than 20% draught with materials processing, dehydrogenation and annealing in a vacuum, under 450-800 ℃, carry out the processing of titanium material, under 600-950 ℃, carry out the processing of alpha titanium alloy material, under 550-900 ℃, carry out the processing of (alpha+beta) Type Titanium Alloy material.
Description
The present invention relates to have the titanium (industrially pure titanium) of superior fatigue strength and processing characteristics or the preparation method of titanium alloy material, particularly relate to and have the thin titanium of axle microstructure or the preparation method of titanium alloy material of waiting.
Because titanium and titanium alloy material have the high specific tenacity ratio of proportion (the high intensity with) and good solidity to corrosion, thus be used to produce aircraft part and as many other materials in addition, and also the purposes of these materials is also in expansion.Here it is, and why titanium material, alpha titanium alloy material and (alpha+beta) Type Titanium Alloy material require have good intensity and ductility.Is very strict to performance demands in relevant field, and particularly the aircraft that uses under repeated stress environment part field in addition not only needs good processibility, but also needs strong fatigability, and stipulated strict quality standard (as referring to AMS4967).In order to satisfy these needs, the microstructure of material must have enough thin α phase equi-axed crystal.
But, in the industrially pure titanium material,,, can not obtain uniform and thin microstructure although can produce equiaxial microstructure by conventional processing and thermal treatment because impurity composition is restricted.
For alpha titanium alloy material and (alpha+beta) Type Titanium Alloy material, be used in the section bar in above-mentioned field, usually make by hot rolling and combined with heat treatment as plate, line, pipe and rod, but, the shortcoming of routine techniques is in hot-rolled process, is fit to (1) and keeps being enough to obtaining having the good workability of high-precision material shape and (2) and produces in material and wait the temperature range of a microstructure very narrow.
In addition, in this temperature range, because variation of temperature, even temperature raises a little, and the microstructure of material is easy to change, grain growth, and microstructure usually is uneven after the thermal treatment.And produce a problem: the microstructure that forms after the hot-work changes very little by follow-up thermal treatment.
Under this background, advised being the α type of axle microstructures such as acquisition has and the following technology of (alpha+beta) Type Titanium Alloy material:
(1) Japan's authorization patent specification NO.63-4914 discloses a kind of method, can heat repeatedly in a specific narrow temperature scope and process in the method.But this method shortcoming is: can not make microstructure enough thin and even, what reached waits the axle property still dissatisfied, and productivity is hanged down and the production cost height.
(2) Japan's authorization patent specification NO.63-4908 discloses a kind of method, in the method can be in the specific range of temperatures heat hot stocking and the thermal treatment of single β phase.Yet this method shortcoming is can not obtain enough all even thin microstructures and the axle property that waits that is reached is unsatisfied with.
Hydrogen improves the processibility of titanium alloy as interim alloying element (hydrogenation) or the technology of microstructure is known by adding, and it is known using the following method of this technology.
(3) people's such as U.Zwicker United States Patent (USP) NO2,892,742(1958,6,30) a kind of method is disclosed, make in the method and containing 6%(weight at least) add 0.05-10%(weight in the alpha titanium alloy of Al) hydrogen improve hot workability, last, make the material dehydrogenation by heating in high vacuum.But the document is not mentioned the microstructure of material.
(4) in " hydrogen is as titanium interalloy element (Hydvovac) " (" titanium ", 80,2477-2486 page or leaf) of people such as W.R.Kerr, point out, if with (alpha+beta) type alloy Ti-6Al-4V hydrogenation, then beta transus temperature reduces, and hot workability is improved, and obtains thin microstructure.But hot-work is undertaken by forging to be not more than 60% draught, and this forging is undertaken by low speed hammer motor system, and the hammer speed of press is low to 1.27 * 10
-3So this method can not be used with technical scale.
(5) at " by in the Ti-6Al-4V alloy, using hydrogen control anisotropy " (Vol.37 of India metal association journal of people such as N.C.Birla, No.5,1984,10, the 631-635 page or leaf) points out, if with Ti-6Al-4V hydrogenation of (alpha+beta) Type Titanium Alloy and hot rolling, the anisotropy of tensile property improves.But, according to this method the hydrogenant plate being carried out 2 hours homogenizing at 990 ℃, is 10% at 730 ℃ with some passage draught per passes then, and overall compression ratio is 50% to be rolled, and the homogenizing of carrying out 10 minutes after each compression is handled, but this method can not be used with technical scale.
The material that can not obtain to have enough thin and equiaxial microstructure by these routine techniquess, and can not stably make titanium and titanium alloy material with technical scale with superior fatigue strength and processibility by these routine techniquess.
An object of the present invention is to provide a kind of method, wherein can make the microstructure of titanium material and α type and (alpha+beta) Type Titanium Alloy material thinner and reach, and these materials with superior fatigue strength and processibility can be stably with industrial-scale production by axle horizontals such as routine techniques are inaccessiable.
This purpose of the present invention can reach by the method for following design.
More precisely, the invention provides a kind of method for preparing titanium material and (alpha+beta) Type Titanium Alloy material, it is characterized in that will be wherein hydrogen richness be 0.02-2%(weight) the material of hydrogenation under 450-900 ℃ of temperature, process with draught, then in a vacuum with material dehydrogenation and annealing simultaneously above 60%.The processing of titanium material is carried out at 450-800 ℃, and the processing of (alpha+beta) Type Titanium Alloy material is carried out at 550-900 ℃.
In addition, the invention provides a kind of method for preparing titanium material and α type and (alpha+beta) Type Titanium Alloy material, it is characterized in that will be wherein hydrogen richness be 0.02-2%(weight) the material of hydrogenation heat-treat, the material heating temperature is not less than beta transus temperature, cooling then, material is processed under 450-950 ℃ of temperature, and draught is not less than 20%, in a vacuum with material dehydrogenation and annealing simultaneously.The processing of titanium material is carried out at 450-800 ℃, and the processing of alpha titanium alloy material is carried out at 600-950 ℃, and the processing of (alpha+beta) Type Titanium Alloy material is carried out at 550-900 ℃.
Fig. 1 and 3 is according to the Photomicrograph of institute of the present invention prepared material (magnification 500);
Fig. 2 and 5 be according to the Photomicrograph of routine techniques institute prepared material (magnification 500) and
Fig. 4 is the Photomicrograph (magnification 500) of comparative material.
In order to solve the problems referred to above of routine techniques, the inventor notices that the hydrogen conduct can be easy to be added in titanium and the titanium alloy, and the element that can be easy to therefrom remove, and has carried out various experiments and research. Found that, if with titanium and titanium alloy hydrogenation, by increasing solid solution hydrogen beta transus temperature is reduced, and hot-working can be carried out being lower than under the temperature of common employing, if after a suitable drafts processing, with the material dehydrogenation, simultaneously recrystallization and annealing can obtain by the inaccessiable material with thin microscopic structure such as axle such as grade of routine techniques in a vacuum.
Material object of the present invention comprises the industrially pure titanium material, such as the titanium material of JIS standard; The alpha titanium alloy material is such as Ti-5Al-2.5Sn and (alpha+beta) Type Titanium Alloy material, such as Ti-6Al-4V. Founding materials, such as ingot casting, by the hot-working material that forging, breaking down, hot rolling, hot extrusion etc. are made, cold rolling material and all can process according to the present invention by the material of powder die forming.
In the present invention, at first by hydrogenation, make in above-mentioned material object to contain 0.02-2%(weight) hydrogen. If hydrogen content is lower than 0.02%(weight), even process under the following conditions, dehydrogenation and annealing, can not obtain to expect thin and wait axle micro-Tissue. Because the increase of hydrogen content, processing can easily be carried out under lower temperature, and the effect that forms thinner microscopic structure improves, if but hydrogen content surpasses 2%(weight), then material itself becomes fragile, the problem of running into during transportation, as the increase of breaking. So hydrogen content is limited in 0.02-2%(weight).
As the method for material hydrogenation, for example can adopt hydrogenation and heat treatment in hydrogeneous atmosphere in the melt, its step and condition are especially not strict. Hydrogen during skewness, can carry out homogenising by heat treatment under suitable temperature in material thereafter.
Narrate processing conditions now.For the titanium material, under 450-800 ℃ of temperature, process with draught above 60%.For (alpha+beta) Type Titanium Alloy material, under 550-900 ℃ of temperature, process with draught above 60%.Because titanium alloy material has the undesirable heat processibility, generally titanium alloy material is being higher than 900 ℃ but be not less than beta transus temperature and process by routine techniques, thus the α grain growth, and be difficult to obtain thin microstructure after processing and the annealing.On the contrary, according to method of the present invention because the hydrogen hydrogenation by above-mentioned amount reduces beta transus temperature, even under the processing temperature that adopts usually, still exist a large amount of β mutually and a small amount of α mutually.Therefore, can solve the problem that the α grain growth causes in routine techniques.In addition, because easily the β of processing exists mutually at a lower temperature in a large number, can process being lower than under the temperature of routine techniques.In addition, if process under above-mentioned specified temp and compression ratio, the microstructure that obtains after the recrystallization annealing is enough thin and wait spool.The upper limit of the processing temperature that sets is the top temperature that reaches above-mentioned effect, and the lower limit of setting is to add man-hour not occur the disruptive minimum temperature.Here the draught of indication is not heat once more to carry out once down or the secondary or the total reduction of processing repeatedly.
In the method for the invention because processing temperature is relatively low and draught up to more than 60%, material deforms and a small amount of α exists mutually, like this, the Be Controlled of growing up of α crystal grain after the processing is carried out cooling period hydride and is separated out with dispersed after the processing.Along with separating out of this hydride,
Produce the high density dislocation net in the material, also produce the high density dislocation net in the hydride itself.So if material dehydrogenation and annealing simultaneously in a vacuum, hydride disappears, and obtain to have the microstructure of a recrystal grain such as enough thin.
Be noted that because alpha titanium alloy material hot workability extreme difference will prepare the material with above-mentioned microstructure, need carry out β thermal treatment as described below as the hot-work pre-treatment.
After the processing, with material dehydrogenation and annealing simultaneously in a vacuum.Heating condition can be to carry out those conditions that recrystallize adopts usually after the processing, but temperature is lower better.If the residual hydrogen amount surpasses certain level, even recrystallize forms thin and equiaxial microstructure, but material becomes fragile, and can not obtain satisfied product.So dehydrogenation is carried out in a vacuum.If the vacuum tightness decompression is about 1 * 10
-1Torr or lower just enough.Pressure lower (vacuum tightness is higher), the treatment time is shorter.Start from the point of view of practical utility, preferably decompression is about 1 * 10
-4Torr is a rare gas element and keep gas, as Ar.
Narrate wherein thermal treatment now as the pre-treatment of above-mentioned processing and the example that carries out.For each of titanium material, alpha titanium alloy material and (alpha+beta) titanium alloy material, by the hydrogenant material being heat-treated (hereinafter referred to as " β thermal treatment "), therefore, material is heated being not less than under the temperature of beta transus temperature, cooling makes the microstructure of material thinner then.When the material hot-work of such processing, draught needn't be greater than 60% under said temperature, and if draught is not less than 20%, dehydrogenation subsequently and annealing make have enough thin with wait a material of recrystallize microstructure.So, even, also can stably prepare material with technical scale with above-mentioned microstructure having under the alpha titanium alloy material situation of poor especially hot workability.
According to this β thermal treatment of the present invention, be not less than heating material under the temperature of beta transus temperature, cooling obtains thin tissue then.Be preferably, Heating temperature is low as far as possible in the β scope.Can adopt that stove is cold, in air cooling and the water-cooled any, but better be cooling at a high speed.If cooling temperature is than the temperature of low 300 ℃ of beta transus temperature, can obtain thin microstructure.After the cooling, material directly carried out above-mentioned processing or material once heated or be cooled to preset temperature, carry out above-mentioned processing then.After the processing, as mentioned above with material dehydrogenation and annealing simultaneously in a vacuum.
Can obviously find out from above-mentioned, according to preparation method of the present invention, can be stably have thin titanium and the titanium alloy material that waits the axle microstructure that routine techniques can not obtain with the technical scale preparation, can stably provide have superior strength, these materials of fatigue characteristic and processibility.
Embodiment
Describe the present invention in detail referring now to following embodiment, but do not limit the scope of the invention.
Embodiment 1
With the hydrogen amount be 0.01,0.05,0.2,0.5,0.9,1.5 or 2.2(weight %) the Ti-6Al-4V alloy flat bloom of hydrogenation is 500,600,700,800 or 950 ℃ of down heating and with 40%, 60%, 70% or 80% draught hot rolling.After the hot rolling, under 700 ℃, in vacuum, carry out dehydrogenation and annealed 1 hour.
The microstructure observation of material the results are shown among the table 1-6 after hot rolling, dehydrogenation and the annealing.Hydrogen richness be 0.05,0.2,0.5,0.9 and 1.5(weight %), Heating temperature is that 600,700 and 800 ℃ and draught are in the hot rolling and annealing material that obtains for 70% and 80% time, its microstructure is enough thin and wait spool.
As an exemplary, will contain 0.2%(weight) material of hydrogen amount is 750 ℃ of heating down, and the draught hot rolling with 80% is 700 ℃ of dehydrogenations and annealed 1 hour.The Photomicrograph of the material microstructure that obtains is shown in Fig. 1.Be noted that at hydrogen content be 2.2%(weight) the material occasion, the hot rolling postcooling is very crisp to the material that room temperature obtains, subsequently in a vacuum annealing can not carry out.
As the example of routine techniques, unhydrided Ti-6Al-4V alloy 950 ℃ of heating and 80% draught hot rollings down, to be annealed then, the microstructure picture that obtains material is shown in Fig. 2.
The material that can see the inventive method preparation has thinner and more equiaxial microstructure than the material that routine techniques prepares.
Table 1
Hydrogen richness 0.01%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ △ △
700 △ △ △ △
800 △ △ △ △
950 X X X X
Zero: fully thin equi-axed crystal microstructure
△: parts of fine equi-axed crystal microstructure
X: coarse-grain or needle-like microstructure
Table 2
Hydrogen richness 0.05%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ ○ ○
700 △ △ ○ ○
800 △ △ ○ ○
950 X X X X
Table 3
Hydrogen richness 0.2%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ ○ ○
700 △ △ ○ ○
800 △ △ ○ ○
900 X X X X
Table 4
Hydrogen richness 0.5%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ ○ ○
700 △ △ ○ ○
800 △ △ ○ ○
950 X X X X
Table 5
Hydrogen richness 0.9%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ ○ ○
700 △ △ ○ ○
800 △ △ ○ ○
950 X X X X
Table 6
Hydrogen richness 1.5%(weight) microstructure of material
Draught (%)
Temperature (℃) 40 60 70 80
500 △ △ △ △
600 △ △ ○ ○
700 △ △ ○ ○
800 △ △ ○ ○
950 X X X X
Embodiment 2
With the hydrogen amount is 0.2%(weight) the Ti-6Al-4V alloy flat bloom of hydrogenation is 850 or 950 ℃ of heating down, the temperature that just is higher than the beta transus temperature under this hydrogen richness, air cooling, process again 500,600,700,750,800 or 950 ℃ of heating down, and with 22%, 40%60% or 80% compression ratio.Then with material in a vacuum 700 ℃ of following dehydrogenations and annealed 1 hour.The microstructure observation of gained material the results are shown in table 7 and table 8.If hot worked Heating temperature is 600,700,750 or 800 ℃, the material after the annealing all has the thin axle microstructure that waits under any draught.
Table 7
Hydrogen richness 0.2%(weight),
Heat down and the refrigerative material microstructure in 850 ℃
Draught (%)
Temperature (℃) 22 40 60 80
500 △ △ △ △
600 ○ ○ ○ ○
700 ○ ○ ○ ○
750 ○ ○ ○ ○
800 ○ ○ ○ ○
950 X X X X
Table 8
Hydrogen richness 0.2%(weight),
Heat down and the refrigerative material microstructure at 950 ℃
Draught (%)
Temperature (℃) 22 40 60 80
500 △ △ △ △
600 ○ ○ ○ ○
700 ○ ○ ○ ○
750 ○ ○ ○ ○
800 ○ ○ ○ ○
950 X X X X
Zero: fully thin equiax crystal microstructure
△: parts of fine equiax crystal microstructure
X: coarse-grain or needle-like microstructure
Embodiment 3
As sample, the slab ingot that 100 millimeters hydrogen richnesss of thickness are different heats being not less than under the beta transus temperature corresponding with hydrogen richness, and cool to room temperature, carries out β thermal treatment with typical alpha titanium alloy Ti-5Al-2.5Sn.With material hot rolling under different heating temperature and compression ratio, then 1 * 10
-4Under the torr vacuum, 700 ℃ with material heating 5 hours so that this material dehydrogenation and carry out recrystallize.
Final microstructure result and the preparation condition that obtains material is shown in table 9.In the evaluation of microstructure, symbol " zero " represents and waits a microstructure that symbol " △ " is represented parts of fine and wait an axle microstructure that symbol " X " is represented coarse grain or elongation crystal grain microstructure carefully complete.Be noted that in test No 14,, break because hot-rolled temperature is low, and can not hot rolling.In test No 16, because the hydrogen richness height, material becomes fragile at hot rolling postcooling state, can not carry out subsequent disposal.
As typical example, test the material of No 8 according to the present invention, the comparative material of test No 13 and under 980 ℃ with 50% draught not the microstructure picture of hydride material repeat-rolling and the common material that obtained in 5 hours 700 ℃ of heating be shown in Fig. 3,4 and 5 respectively.
As can be seen, can obtain to have the thin α type alloy that waits the axle microstructure according to the present invention.
Embodiment 4
Carry out hot rolling with quadrat method with the industrially pure titanium material of JIS2 level such as embodiment 3 are described, and will not carry out the heat treated material of β 1 * 10
-4Heat 1 hour down up to dehydrogenation and annealing in 600 ℃ in the torr vacuum.The results are shown in table 10(and do not carry out β thermal treatment) and show 11(and carry out β thermal treatment).Test No.14 in the table 10 and the test No.15 in the table 11 because hot-rolled temperature is low, break, can not be rolling.In the test No.17 of the test No.17 of table 10 and table 11,, can not carry out subsequent disposal because the hydrogen richness height is very crisp at cooling attitude material after the hot rolling.
As can be seen, can obtain to have the thin titanium material that waits the axle microstructure according to the present invention.
In the above-described embodiments, the sheet material of rolling slab ingot and inspection formation.Be proved at the rod that is formed by rolling blank, line and section bar, by the various section bars that the hot extrusion blank forms, it is similar forging the result who is obtained under the situation of material and powder shaping material.
Table 10
JIS2 level titanium (it is heat treated not carry out β)
Test hydrogen richness hot-rolled temperature draught microstructure evaluation classification
No (weight %) (℃) (%)
1 0.02 800 90 zero the present invention
2 0.3 750 80 zero the present invention
3 0.3 680 70 zero the present invention
4 0.3 600 65 zero the present invention
5 0.5 750 65 zero the present invention
6 0.5 680 65 zero the present invention
7 0.5 600 65 zero the present invention
8 0.5 600 95 zero the present invention
9 0.5 500 75 zero the present invention
10 1.0 700 80 0 the present invention
11 1.0 450 65 0 the present invention
12 2.0 450 65 0 the present invention
13 0.01 800 90 X relatively
14 0.5 400--relatively
15 0.5 850 90 X relatively
16 0.5 600 60 △ relatively
17 2.2 450 65-relatively
Table 11
JIS2 level titanium (it is heat treated to carry out β)
The classification of test hydrogen richness β thermal treatment hot-rolled temperature draught microstructure
Temperature is estimated
No (weight %) (℃) (℃) (%)
1 0.02 900 800 90 zero the present invention
2 0.3 800 750 80 zero the present invention
3 0.3 800 680 60 zero the present invention
4 0.3 800 600 40 zero the present invention
5 0.5 750 750 60 zero the present invention
6 0.5 750 680 40 zero the present invention
7 0.5 750 600 20 zero the present invention
8 0.5 750 600 40 zero the present invention
9 0.5 750 600 70 zero the present invention
10 0.5 750 500 50 0 the present invention
11 1.0 700 700 70 0 the present invention
12 1.0 700 450 30 0 the present invention
13 2.0 650 450 20 0 the present invention
14 0.01 900 800 90 X relatively
15 0.5 750 400--relatively
16 0.5 750 850 95 △ relatively
17 2.2 650 450 20-relatively
Claims (7)
1, a kind of preparation has the titanium of axle microstructure such as thin and the method for titanium alloy material, this method comprises that processing is titanium or (alpha+beta) Type Titanium Alloy material of 0.02-0.2% (weight) hydrogenation with the hydrogen amount, this material is processed dehydrogenation and annealing in a vacuum simultaneously to surpass 60% draught under 450-900 ℃ of temperature.
2, according to the process of claim 1 wherein processing titanium material under 450-800 ℃ of temperature.
3, according to the process of claim 1 wherein processing (alpha+beta) Type Titanium Alloy material under 550-900 ℃ of temperature.
4, a kind of preparation has the titanium of axle microstructure such as thin and the method for titanium alloy material, this method comprises being 0.02-2%(weight with the hydrogen amount) titanium, alpha titanium alloy or (alpha+beta) Type Titanium Alloy material of hydrogenation heat-treat, material is heated being not less than under the temperature of beta transus temperature, cooling then, this material is processed dehydrogenation and annealing in a vacuum simultaneously to be not less than 20% draught under 450-950 ℃ of temperature.
5, according to the method for claim 4, wherein under 450-800 ℃ of temperature, process the titanium material.
6, according to the method for claim 4, wherein under 600-950 ℃ of temperature, process the alpha titanium alloy material.
7, according to the method for claim 4, wherein process (alpha+beta) Type Titanium Alloy material down at 550-900 ℃.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP65982/89 | 1989-03-20 | ||
| JP1065982A JPH0726183B2 (en) | 1988-12-28 | 1989-03-20 | Method for producing α + β type titanium alloy having a fine and equiaxed structure |
| JP26631189A JPH03130352A (en) | 1989-10-16 | 1989-10-16 | Production of titanium or alpha titanium alloy having fine and equiaxial structure |
| JP266311/89 | 1989-10-16 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1046565A true CN1046565A (en) | 1990-10-31 |
| CN1019205B CN1019205B (en) | 1992-11-25 |
Family
ID=26407144
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN90102119A Expired CN1019205B (en) | 1989-03-20 | 1990-03-20 | Method for preparing titanium and titanium alloy material with fine equiaxial microstructure |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US5092940A (en) |
| EP (1) | EP0388830A1 (en) |
| CN (1) | CN1019205B (en) |
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| CN102342866A (en) * | 2010-07-30 | 2012-02-08 | 中国科学院金属研究所 | Artificial-titanium auditory ossicle |
| JP5168434B2 (en) * | 2011-04-22 | 2013-03-21 | 新日鐵住金株式会社 | Titanium slab for hot rolling and manufacturing method thereof |
| US10920307B2 (en) * | 2017-10-06 | 2021-02-16 | University Of Utah Research Foundation | Thermo-hydrogen refinement of microstructure of titanium materials |
| CN109777978A (en) * | 2019-01-10 | 2019-05-21 | 昆明理工大学 | One kind setting hydrogen methods based on zone-melting titanium alloy |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2892742A (en) * | 1956-06-22 | 1959-06-30 | Metallgesellschaft Ag | Process for improving the workability of titanium alloys |
| US4415375A (en) * | 1982-06-10 | 1983-11-15 | Mcdonnell Douglas Corporation | Transient titanium alloys |
| JPS634908A (en) * | 1986-06-25 | 1988-01-09 | 松下電工株式会社 | Method of reinforcing end section of building board |
| JPS634914A (en) * | 1986-06-26 | 1988-01-09 | Asahi Chem Ind Co Ltd | Manufacture of film |
| US4680063A (en) * | 1986-08-13 | 1987-07-14 | The United States Of America As Represented By The Secretary Of The Air Force | Method for refining microstructures of titanium ingot metallurgy articles |
-
1990
- 1990-03-16 US US07/494,754 patent/US5092940A/en not_active Expired - Fee Related
- 1990-03-19 EP EP90105106A patent/EP0388830A1/en not_active Withdrawn
- 1990-03-20 CN CN90102119A patent/CN1019205B/en not_active Expired
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102248178A (en) * | 2011-07-06 | 2011-11-23 | 郑新科 | Process for preparing 6AI4V titanium alloy powder by using mechanical alloying heat treatment method |
| CN109252121A (en) * | 2018-10-30 | 2019-01-22 | 江苏希诺实业有限公司 | A kind of processing method of the pure titanium article surface acicular crystal decorative pattern of thin-walled |
| CN109252121B (en) * | 2018-10-30 | 2021-07-20 | 希诺股份有限公司 | Processing method of needle-shaped crystal patterns on surface of thin-wall pure titanium product |
| CN113874534A (en) * | 2019-03-16 | 2021-12-31 | 普拉西斯粉末技术股份有限公司 | Microstructure improvement of titanium alloy |
| CN112251637A (en) * | 2020-09-29 | 2021-01-22 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Fe alloy and preparation method thereof |
| CN112251637B (en) * | 2020-09-29 | 2022-05-10 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Fe alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| EP0388830A1 (en) | 1990-09-26 |
| CN1019205B (en) | 1992-11-25 |
| US5092940A (en) | 1992-03-03 |
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